Optical glass

ABSTRACT

A high-refractivity low-dispersion optical glass that can be stably supplied and has excellent glass stability and that has coloring reduced, composed of in mass %, 5 to 32% of total of SiO 2  and B 2 O 2 , 45 to 65% of total of La 2 O 2 , Gd 2 O 2  and Y 2 O 2 , 0.5 to 10% of ZnO, 1 to 20% of total of TiO 2  and Nb 2 O 5 , and optionally other components. The optical glass has a refractive index nd of 1.89 to 2.0, an Abbe&#39;s number νd of 32 to 38 and a coloring degree λ70 of 430 nm or less.

This application is a divisional of application Ser. No. 13/358,748,filed Jan. 26, 2012, now allowed, which in turn is a divisional ofapplication Ser. No. 12/570,436 filed Sep. 30, 2009, now U.S. Pat. No.8,127,570, which in turn claims priority of Japanese application SerialNo. 2008-253900 filed Sep. 30, 2008, the entire content of which ishereby incorporated by reference in this application.

TECHNICAL FIELD

This invention relates to an optical glass having high-refractivitylow-dispersion properties, a press-molding glass gob and an opticalelement formed of the above optical glass each, and processes forproducing an optical element blank and an optical element.

BACKGROUND ART

When combined with a lens formed of a high-refractivity high-dispersionglass, a lens formed of a high-refractivity low-dispersion glass ensuresthat an optical system can be downsized while correcting chromaticaberration. It hence occupies an important place as an optical elementconstituting an image-sensing optical system and a projection opticalsystem such as a projector, etc.

JP 2007-269584 A discloses such a high-refractivity low-dispersionglass. The glass disclosed in JP 2007-269584A has a refractive index ndof 1.75 to 2.00 and has a Ta₂O₅ content in the range of 0 to 25 mass %.However, all of the glasses that have a refractive index nd of at least1.85 contain a large amount of Ta₂O₅. That is because it isindispensable to introduce a large amount of Ta₂O₅ for securing glassstability in the high refractivity region such as a refractive index ndof 1.75 or more. For such a high-refractivity low-dispersion glass,therefore, Ta₂O₅ is a main and essential component.

DISCLOSURE OF THE INVENTION Problems to be Solved by the Invention

Meanwhile, tantalum (Ta) is an element having a high rarity value and isin itself a very expensive substance. Moreover, rare metal prices arerecently soaring worldwide, and the supply of tantalum is deficient. Inthe field of glass production, tantalum as a raw material is alsodeficient, and if such a situation continues, it may be no longerpossible to maintain the stable supply of high-refractivitylow-dispersion glasses that are essential and indispensable in theindustry of optical apparatuses. Similarly, germanium (Ge) is asubstance that increases the refractive index without impairing theglass stability when used as a glass component, while it is a moreexpensive substance than tantalum, and it is required to decrease itsuse in amount.

Meanwhile, the optical element for constituting the image-sensingoptical system or the projection optical system requires a remarkablycoloring-free glass material. These optical systems use a plurality oflens for correcting various aberrations, and when the transmitted lightquantity per lens is not sufficient, the transmitted light quantity ofthe entire optical system is greatly decreased. In particular, aninterchangeable lens of a single-lens reflex camera has a large apertureas compared with a lens of a compact camera and has a large thicknessitself, so that when a glass having a poor coloring degree is used, thetransmitted light quantity of the entire interchangeable lens is sharplydecreased. For these reasons, an optical glass whose coloring is reducedis required in order to make the most of the high-refractivitylow-dispersion properties.

Under the circumstances, it is an object of this invention to provide ahigh-refractivity low-dispersion optical glass that can be stablysupplied and has excellent glass stability, a press-molding glass goband an optical element that are formed of the above glass, and processesfor the production of an optical element blank and an optical element.

Means to Solve the Problems

For achieving the above object, the present inventors have made diligentstudies and as a result have found that the above object can be achievedby an optical glass having a specified glass composition, a specifiedrefractive index and a specified Abbe's number, and the presentinvention has been accordingly completed on the basis of this finding.

That is, this invention provides

(1) an optical glass comprising, by mass %,

5 to 32% of total of SiO₂ and B₂O₃,

45 to 65% of total of La₂O₃, Gd₂O₃ and Y₂O₃,

0.5 to 10% of ZnO,

1 to 20% of total of TiO₂ and Nb₂O₅,

0 to 15% of ZrO₂,

0 to 2% of WO₃,

0 to 20% of Yb₂O₃,

0 to 10% of total of Li₂O, Na₂O and K₂O,

0 to 10% of total of MgO, CaO, SrO and BaO,

0 to 12% of Ta₂O₅,

0 to 5% of GeO₂,

0 to 10% of Bi₂O₃, and

0 to 10% of Al₂O₃,

wherein the mass ratio of the content of SiO₂ to the content of B₂O₂,(SiO₂/B₂O₂), is from 0.3 to 1.0, and the mass ratio of the total contentof Gd₂O₃ and Y₂O₃ to the total content of La₂O₂, Gd₂O₃ and Y₂O₃,(Gd₂O₃+Y₂O₃)/(La₂O₂+Gd₂O₃+Y₂O₂), is from 0.05 to 0.6,

the optical glass having a refractive index nd of 1.89 to 2.0 and anAbbe's number νd of 32 to 38 and having a coloring degree λ70 of 430 nmor less,

(2) an optical glass of the above (1), which contains 2 to 15% of SiO₂and 6 to 30% of B₂O₃.

(3) an optical glass of the above (1) or (2), which contains 25 to 65%of La₂O₃, 0 to 25% of Gd₂O₃ and 0 to 20% of Y₂O₃,

(4) an optical glass of any one of the above (1) to (3), which contains0.1 to 15% of TiO₂ and 0.1 to 15% of Nb₂O₅,

(5) an optical glass of any one of the above (1) to (4), which contains0.5 to 15% of ZrO₂,

(6) an optical glass of any one of the above (1) to (5), which has aTa₂O₅ content of 0 to 10%,

(7) an optical glass of any one of the above (1) to (6), which is aGe-free glass,

(8) an optical glass of any one of the above (1) to (7), which has aliquidus temperature of 1,300° C. or lower,

(9) an optical glass of any one of the above (1) to (8), which has aglass transition temperature of 710° C. or lower,

(10) a press-molding glass gob formed of the optical glass recited inany one of the above (1) to (9),

(11) an optical element formed of the optical glass recited in any oneof the above (1) to (9),

(12) a process for producing an optical element blank that is completedinto an optical element by grinding and polishing,

which comprises heating, softening and press-molding the press-moldingglass gob recited in the above (10),

(13) a process for producing an optical element blank that is completedinto an optical element by grinding and polishing,

which comprises melting glass raw materials, press-molding the resultantmolten glass and producing the optical element blank formed of theoptical glass recited in any one of the above (1) to (9),

(14) a process for producing an optical element, which comprisesproducing an optical element blank by the process recited in the above(12) or (13), and grinding and polishing said optical element blank, and

(15) a process for producing an optical element, which comprises heatingthe glass gob recited in the above (10) and precision press-molding thesame.

Effect of the Invention

According to this invention, there can be provided a high-refractivitylow-dispersion optical glass that can be stably supplied and hasexcellent glass stability, a press-molding glass gob and an opticalelement that are formed of the above glass, and processes for theproduction of an optical element blank and an optical element.

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1 is a graph showing a relationship between the temperatures ofre-heating and the number density of crystals precipitated inside aglass with regard to the glass obtained in Example 1.

FIG. 2 is a graph showing a schedule of heating a glass gob in Example4.

BEST MODE OF THE INVENTION [Optical Glass]

First, the optical glass of this invention will be explained below.

This invention seeks to provide a high-refractivity low-dispersionoptical glass in which the amounts of Ta₂O₅ and GeO₂, especiallyexpensive components of glass components, are reduced or limited. Whenthe amount of Ta₂O₅ or GeO₂ is simply reduced, a glass is not formed ora glass devitrifies and is no longer usable, and it is difficult toimpart an optical glass with the high-refractivity low-dispersionproperties while maintaining its devitrification resistance. Fordecreasing the amounts of Ta₂O₅ and GeO₂ to be introduced whileovercoming the above problem, the apportionment of components forimparting high refractivity is essential.

In this invention, B₂O₃ and SiO₂ are introduced as oxides for forming aglass network, and (a) at least one of La₂O₂, Gd₂O₂ and Y₂O₂, (b) ZnOand (c) at least one of TiO₂ and Nb₂O₅ are incorporated to be co-presentas essential components. In this invention, ZnO is an essentialcomponent that not only contributes to an improvement in meltability anda decrease in glass transition temperature but also contributes toimpartment with high-refractivity low-dispersion and an improvement indevitrification resistance.

On the basis of the above formulation, a balance between the content ofB₂O₃ and the content of SiO₂ is adjusted to improve the meltability andthe moldability of a molten glass, and their balance with othercomponents is adjusted.

When the meltability and glass stability are improved, an increase inthe melting temperature of a glass can be inhibited, which keeps theglass from eroding materials that constitute a glass melting vessel. Asa result, the amount of substances that deteriorate the coloring such asplatinum ion to be melted into a molten glass can be reduced orinhibited, and a glass whose coloring is reduced can be obtained.

Further, the coloring of the glass is inhibited by restricting the upperlimit of the total content of TiO₂ and Nb₂O₅ that improve the glassstability. On the basis of these findings, this invention has achievedthe above object.

The optical glass of this invention comprises, by mass %,

5 to 32% of total of SiO₂ and B₂O₃.

45 to 65% of total of La₂O₃, Gd₂O₃ and Y₂O₃,

0.5 to 10% of ZnO,

1 to 20% of total of TiO₂ and Nb₂O₅,

0 to 15% of ZrO₂,

0 to 2% of WO₃,

0 to 20% of Yb₂O₃,

0 to 10% of total of Li₂O, Na₂O and K₂O,

0 to 10% of total of MgO, CaO, SrO and BaO,

0 to 12% of Ta₂O₅.

0 to 5% of GeO₂.

0 to 10% of Bi₂O₃, and

0 to 10% of Al₂O₃,

wherein the mass ratio of the content of SiO₂ to the content of B₂O₃,(SiO₂/B₂O₃), is from 0.3 to 1.0, and the mass ratio of the total contentof Gd₂O₃ and Y₂O₃ to the total content of La₂O₃, Gd₂O₃ and Y₂O₃,(Gd₂O₃+Y₂O₃)/(La₂O₃+Gd₂O₃+Y₂O₃), is from 0.05 to 0.6,

the optical glass having a refractive index nd of 1.89 to 2.0 and anAbbe's number νd of 32 to 38 and having a coloring degree λ70 of 430 nmor less.

(Reasons for Limiting Compositional Range)

The reasons for limiting the compositional ranges of the optical glassof this invention will be explained below, while the content of eachcomponent and each total content depicted by % are based on mass %unless otherwise specified.

Both SiO₂ and B₂O₃ are network-forming oxides, and they are essentialcomponents for maintaining the glass stability. When the total contentof SiO₂ and B₂O₃ is less than 5%, it is difficult to maintain glassstability, and the glass is liable to devitrify during production. Whenthe above total content exceeds 32%, the refractive index is decreased.The total content of SiO₂ and B₂O₃ is hence limited to 5 to 32%. Thetotal content of SiO₂ and B₂O₃ is preferably in the range of 5 to 30%,more preferably 7 to 28%, still more preferably 9 to 25%, yet morepreferably 12 to 23%.

Of the network-forming oxides, SiO₂ has an effect on the maintaining ofglass stability, the maintaining of a viscosity suitable for molding amolten glass, the improvement of chemical durability, etc. When it isintroduced to excess, it is difficult to achieve the desired refractiveindex and Abbe's number, the liquidus temperature and glass transitiontemperature are increased, or the meltability and devitrificationresistance of the glass are deteriorated.

B₂O₃ has an effect on the maintaining of the meltability of the glass,the inhibition of the liquidus temperature from increasing and theimpartment with a low dispersion property. When it is introduced toexcess, the glass stability is deteriorated, it is difficult to obtainthe desired refractive index, and the chemical durability isdeteriorated.

On the condition that the total content of SiO₂ and B₂O₃ is determinedas described above, for realizing the desired optical properties and atthe same time achieving the maintenance of glass stability, themaintenance of a viscosity suitable for molding a molten glass, animprovement in chemical durability, the inhibition of the liquidustemperature and glass transition temperature from increasing and animprovement in meltability, it is required to adjust a balance betweenthe content of SiO₂ and the content of B₂O₃.

When the mass ratio of the content of SiO₂ to the content of B₂O₃(SiO₂/B₂O₃) is less than 0.3, the glass stability decreases, it isdifficult to maintain the viscosity suitable for molding a molten glass,and the chemical durability tends to decrease. When the above mass ratio(SiO₂/B₂O₃) exceeds 1.0, the liquidus temperature and the glasstransition temperature increase, or the meltability and devitrificationresistance of a glass are deteriorated. Further, it is difficult toimpart the low-dispersion property. The mass ratio of the content ofSiO₂ to the content of B₂O₃ (SiO₂/B₂O₃) is hence adjusted to from 0.3 to1.0. The mass ratio (SiO₂/B₂O₃) is preferably in the range of from 0.3to 0.9, more preferably from 0.4 to 0.7, still more preferably from 0.4to 0.8.

For achieving the maintenance of glass stability, the maintenance of aviscosity suitable for molding a molten glass, an improvement inchemical durability, the inhibition of the liquidus temperature andglass transition temperature from increasing and an improvement inmeltability, preferably, the content of SiO₂ is adjusted to 2 to 15%,and the content of B₂O₃ is adjusted to 6 to 30. The content of SiO₂ ispreferably in the range of 4 to 13%, more preferably 5 to 12%,particularly preferably 5 to 10%. The content of B₂O₃ is preferably inthe range of 6 to 25%, more preferably 8 to 20%, particularly preferably9 to 15%.

When the content of SiO₂ and the content of B₂O₃ are adjusted to theabove ranges, the meltability of the glass and the glass stability areimproved. Therefore, the melting temperature can be inhibited fromincreasing, the erosion of refractory materials constituting aglass-melting vessel, such as platinum, is inhibited, and the coloringby the inclusion of an erosion product such as platinum ion in the glasscan be inhibited or reduced.

La₂O₂, Gd₂O₂ and Y₂O₂ are not only components for impartinghigh-refractivity low-dispersion properties but also components forimparting a high refractive index, and they are also components thathardly color the glass. Therefore, if the total content of La₂O₂, Gd₂O₂and Y₂O₂ can be increased while the glass stability is maintained, it isvery effective for realizing a high-refractivity low-dispersion glasswhose coloring is reduced. In this invention, the glass stability isimproved by optimizing the allocation of La₂O₂, Gd₂O₂ and Y₂O₂ andintroducing at least one of TiO₂ and Nb₂O₅ as will be described later,the total content of La₂O₂, Gd₂O₂ and Y₂O₂ can be increased. Themeasures that are taken as described above can be also factors that canrealize the high-refractivity low-dispersion glass whose coloring isreduced.

When the total content of La₂O₂, Gd₂O₂ and Y₂O₂ is less than 45%, notonly it is difficult to realize the desired refractive index anddispersion, but also the chemical durability decreases. When the abovetotal content exceeds 65%, the liquidus temperature increases, and thedevitrification resistance is deteriorated. Further, since the viscosityduring molding of a molten glass is decreased, the moldabilitydecreases. The total content of La₂O₂, Gd₂O₂ and Y₂O₂ is hence limitedto 45 to 65%. The total content of La₂O₂, Gd₂O₂ and Y₂O₂ is preferablyin the range of 47 to 63%, more preferably 49 to 61%, still morepreferably 51 to 60%.

Of La₂O₃, Gd₂O₃ and Y₂O₃, it is La₂O₃ that most effectively works toincrease the refractive index while maintaining the glass stability.Since, however, the optical glass of this invention is required to havea high refractive index while maintaining the low dispersion property,it is difficult to secure the sufficient glass stability through the useof only La₂O₃ among the above three components. In this invention,therefore, a glass excellent in stability in spite of being ahigh-refractivity low-dispersion glass is realized by making the contentof La₂O₃ the largest among the three components and at the same timecausing La₂O₃ and Gd₂O₃ to be co-present or causing La₂O₃ and Y₂O₃ to beco-present.

For the above reason, the mass ratio of the total content of Gd₂O₃ andY₂O₃ to the total content of La₂O₃, Gd₂O₃ and Y₂O₃,(Gd₂O₃+Y₂O₃)/(La₂O₃+Gd₂O₃+Y₂O₃)_(f) is determined to be from 0.05 to0.6. When the above mass ratio is outside the above range, the glassstability decreases, and when a molten glass is molded, the viscositydecreases and the moldability is impaired. For improving the glassstability more, the mass ratio of (Gd₂O₃+Y₂O₃)/(La₂O₃+Gd₂O₃+Y₂O₃) ispreferably brought into the range of from 0.1 to 0.5, more preferablybrought into the range of from 0.1 to 0.4, still more preferably broughtinto the range of from 0.1 to 0.3.

Further, for obtaining a glass excellent in glass stability, the massratio of the content of Gd₂O₃ to the total content of Gd₂O₃ and Y₂O₃,(Gd₂O₃)/(Gd₂O₃+Y₂O₃), is preferably brought into the range of from 0.1to 1, more preferably brought into the range of from 0.3 to 1, stillmore preferably brought into the range of from 0.5 to 1.

In a preferred embodiment of this invention, the content of La₂O₃ islimited to 25 to 65%, the content of Gd₂O₃ is limited to 0 to 25%, andthe content of Y₂O₃ is limited to 0 to 20%. When the total content ofLa₂O₃, Gd₂O₃ and Y₂O₃ and the allocation of La₂O₃, Gd₂O₃ and Y₂O₃ arebrought into the above ranges, preferably, when the contents of La₂O₃,Gd₂O₃ and Y₂O₃ are brought into the above ranges, the glass stability ismore improved, and the moldability of a molten glass is more improved.Further, the glass melting temperature can be inhibited from increasing,and it can prevent a glass from eroding platinum or a platinum alloyconstituting a melting vessel and can consequently prevent platinum orplatinum alloy from being dissolved as an ion in the glass to color itor from being included as a solid in the glass.

The content of La₂O₃ is preferably in the range of 30 to 60%, morepreferably 30 to 58%, still more preferably 32 to 55%. The content ofGd₂O₃ is preferably in the range of 0.1 to 20%, more preferably 1 to18%, still more preferably 2 to 15%, yet more preferably 5 to 15%,further more preferably 7 to 15%. The content of Y₂O₃ is more preferably0.1 to 18%, more preferably 0.1 to 16%, still more preferably 0.1 to10%.

ZnO is an essential component for realizing the high-refractivitylow-dispersion properties, and it works to improve the meltability anddevitrification resistance of the glass and to decrease the liquidustemperature and glass transition temperature. When the content of ZnO isless than 0.5%, the refractive index decreases, the liquidus temperatureincreases, and the devitrification resistance deteriorates. Further, theglass transition temperature increases, and it is required to increasethe temperature employed for annealing the glass and the temperature forheating and softening the glass when it is press-molded. When the abovecontent exceeds 10%, it is difficult to realize the desired refractiveindex. The content of ZnO is therefore limited to 0.5 to 10%. Thecontent of ZnO is preferably in the range of 1 to 10%, more preferably 1to 8%.

Both of TiO₂ and Nb₂O₅ are components that greatly work to increase therefractive index. When it is intended to increase the refractive indexby only rare earth oxide components such as La₂O₃, Gd₂O₃ and Y₂O₃, theglass stability decreases and the glass is hard to produce. When therare earth oxides and at least one of TiO₂ and Nb₂O₅ are caused to beco-present, the refractive index can be increased while the glassstability is maintained. Further, when at least one of TiO₂ and Nb₂O₅ isintroduced, the glass is improved in chemical durability. For producingthe above effects, the total content of TiO₂ and Nb₂O₅ is adjusted to 1%or more. When the above total content exceeds 20%, not only the liquidustemperature increases, but also the viscosity during molding a moltenglass decreases to deteriorate the moldability. Further, since the glasstransition temperature increases, it is required to increase theannealing temperature, and it is also required to increase the heatingtemperature when glass materials are heated and press-molded, so that anannealing apparatus and a press mold are greatly thermally deteriorated.Further, the coloring of the glass is intensified. The total content ofTiO₂ and Nb₂O₅ is hence limited to 0 to 20%. The total content of TiO₂and Nb₂O₅ is preferably in the range of 2 to 20%, more preferably 2 to18%, still more preferably 2 to 16%.

The content of TiO₂ is preferably adjusted to 0.1% or more forincreasing the refractive index and improving the chemical durabilityand devitrification resistance, and it is preferably adjusted to 15% orless for keeping the liquidus temperature and glass transitiontemperature low. Therefore, the content of TiO₂ is preferably in therange of 0.1 to 15%, more preferably 2 to 13%, still more preferably 2to 9%.

The content of Nb₂O₅ is adjusted to 0.1% or more for increasing therefractive index, further decreasing the liquidus temperature andfurther improving the devitrification resistance. When the content ofNb₂O₅ exceeds 15%, a tendency to an increase in liquidus temperature, atendency to higher dispersion and a tendency to coloring of the glassbegin to appear, so that the content of Nb₂O₅ is preferably limited tothe range of 0.1 to 15%. The content of Nb₂O₅ is more preferably in therange of 1 to 15%, still more preferably 1 to 13%, yet more preferably 1to 9%.

In this invention, the optical glass is preferably an optical glasshaving a co-presence of TiO₂ and Nb₂O₅ as glass components, and such aglass exhibits excellent glass stability while it is a high refractivityglass.

ZrO₂ has the effect of increasing the refractive index and improving thechemical durability. Even when it is introduced in a small amount, theabove excellent effect is produced. However, when the content thereofexceeds 15%, the glass transition temperature and liquidus temperatureincrease, and the devitrification resistance is decreased. The contentof ZrO₂ is hence limited to 0 to 15%. In a preferred embodiment ofoptical glass of this invention, the content of ZrO₂ is adjusted to 0.5to 15%. The content of ZrO₂ is more preferably in the range of 0.5 to13%, still more preferably 1 to 11%, particularly preferably 2 to 9%.

WO₃ is a component that increases the refractive index, decreases theliquidus temperature and contributes to an improvement indevitrification resistance. When the content of WO₃ exceeds 2%, theliquidus temperature increases, and the devitrification resistancedeteriorates. Further, the coloring of the glass is intensified. Thecontent of WO₃ is hence limited to 0 to 2%. The content of WO₃ ispreferably in the range of 0 to 1.5%, more preferably 0 to 1%, stillmore preferably 0 to 0.5%. When the coloring of the glass is taken intoconsideration, it is yet more preferred to incorporate no WO₃.

Yb₂O₃ works to increase the refractive index, and when it is caused tobe co-present with La₂O₃, it works to decrease the liquidus temperatureand to greatly improve the devitrification resistance. When the contentthereof exceeds 20%, the liquidus temperature increases, and thedevitrification resistance deteriorates. The content of Yb₂O₃ is hencelimited to 0 to 20%. The content of Yb₂O₃ is preferably in the range of0 to 18%, more preferably 0 to 16%, still more preferably 0 to 14%, yetmore preferably 0 to 8%, further more preferably 0 to 5%, still furthermore preferably 0 to 2%, yet further more preferably 0 to 1%. However,Yb₂O₃ is an expensive component as compared with La₂O₃, La₂O₃, Gd₂O₃ andY₂O₃, and sufficient glass stability can be obtained without Yb₂O₃, sothat Yb₂O₃ may not be introduced. In this case, there can be producedthe effect of reducing a glass production cost.

Li₂O, Na₂O and K₂O are optional components that works to improve themeltability and to decrease the glass transition temperature. When thetotal content of Li₂O, Na₂O and K₂O exceeds 10%, it is difficult torealize the desired refractive index, and the chemical durability alsodeteriorates. The total content of Li₂O, Na₂O and K₂O is hence limitedto 0 to 10%. The total content of Li₂O, Na₂O and K₂O is preferably inthe range of 0 to 8%, more preferably 0 to 6%, still more preferably 0to 4%, yet more preferably 0 to 2%. When it is sought to impart theglass with a higher refractive index while maintaining the glassstability, it is further preferred to incorporate none of the abovealkali metal oxides.

MgO, CaO, SrO and BaO work to improve the meltability of the glass andto improve the transmittance of the glass in the visible region. Whenintroduced in the form of carbonates or nitrates, they also produce adefoaming effect. However, when the total content thereof exceeds 10%,the liquidus temperature increases, and the devitrification resistancedeteriorates. Moreover, the refractive index decreases, and the chemicaldurability deteriorates. The total content of MgO, CaO, SrO and BaO ishence limited to 0 to 10%. The total content of MgO, CaO, SrO and BaO ispreferably in the range of 0 to 8%, more preferably 0 to 6%, still morepreferably 0 to 4%, yet more preferably 0 to 2%, further more preferably0 to 1%. When it is sought to impart the glass with a higher refractiveindex while maintaining the glass stability, it is still further morepreferred to incorporate none of the alkaline earth metal oxides.

Ta₂O₅ is a component remarkably effective for imparting the glass withhigh-refractivity low-dispersion properties and improving the glassstability. Since, however, it is a very expensive component, the contentthereof is limited to 12% or less for achieving the stable supply of thehigh-refractivity low-dispersion glass that is the object of thisinvention. When the content of Ta₂O₅ is limited to the above range, therefractive index decreases, or the glass stability greatly decreases.However, when at least one of TiO₂ and Nb₂O₅ is incorporated or whenboth of TiO₂ and TiO₂ are incorporated, the content of Ta₂O₅ can bedecreased without impairing the high-refractivity low-dispersionproperties and the glass stability.

Further, when the content of Ta₂O₅ exceeds 12%, the liquidus temperatureincreases, and the devitrification resistance deteriorates. The contentof Ta₂O₅ is hence limited to 0 to 12%. The content of Ta₂O₅ ispreferably in the range of 0 to 10%, more preferably 0 to 8%, still morepreferably 0 to 8%, yet more preferably 0 to 6%, further more preferably0 to 4%, still further more preferably 0 to 2%, yet further morepreferably 0 to 1%, and no content of Ta₂O₅ is particularly preferred.

However, when it has priority to improve the glass stability more, it ispreferred to introduce a small amount of Ta₂O₅. When a small amount ofTa₂O₅ is introduced, not only the glass stability can be more improved,but also the content of La₂O₂ can be decreased while maintaining a highrefractive index, so that the temperature for melting the glass can bedecreased. When the melting temperature is decreased, the erosion of amelting vessel and the coloring of the glass can be decreased orinhibited as already described.

In this case, the content of Ta₂O₅ is preferably in the range of 0.5 to12%, more preferably 1 to 12%, still more preferably 2 to 12%.

GeO₂ is a network-forming oxide and works to increase the refractiveindex, so that it is a component that maintains the glass stability andat the same time can increase the refractive index. However, it is avery expensive component, and it is a component of which the reductionin amount is desirable together with the Ta component. In thisinvention, the composition is determined as explained above, so thateven if the content of GeO₂ is limited to 5% or less, both therealization of the desired optical properties and the realization of theglass stability can be satisfied. The content of GeO₂ is hence limitedto 0 to 5%. The content of GeO₂ is preferably in the range of 0 to 3%,more preferably 0 to 2.5%, still more preferably 0 to 2%, yet morepreferably 0 to 1.5%, further more preferably 0 to 1%, still furthermore preferably 0 to 0.5%. Containing no GeO₂, that is, being a Ge-freeglass is particularly preferred. Since GeO₂ is a network-forming oxideas described above, it can be said that an optical glass of which theGeO₂ content is limited as described above differs in basic compositionfrom an optical glass that realizes high-refractivity low-dispersionproperties on the premise that a predetermined amount or more of GeO₂ iscontained. Further, GeO₂ is a specific component that maintains theglass stability and at the same time can increase the refractive index,and it has a remarkably deep significance to provide an optical glasshaving the above refractive index and Abbe's number and having excellentstability while the amount of expensive GeO₂ in use is limited.

Bi₂O₃ works to increase the refractive index and also to improve theglass stability. However, when the content thereof exceeds 10%, thelight transmittance in the visible region decreases, and the glass tendsto be colored. The content of Bi₂O₃ is hence limited to 0 to 10%. Thecontent of Bi₂O₃ is preferably in the range of 0 to 5%, more preferably0 to 2%, still more preferably 0 to 1%, and no content of Bi₂O₃ isparticularly preferred.

Al₂O₃ works to improve the glass stability and chemical durability asfar as its content is small. However, when its content exceeds 10%, theliquidus temperature increases, and the devitrification resistancedeteriorates. The content of Al₂O₃ is hence limited to 0 to 10%. Thecontent of Al₂O₃ is preferably in the range of 0 to 5%, more preferably0 to 2%, still more preferably 0 to 1, and no content of Al₂O₃ isparticularly preferred.

Sb₂O₃ can be added as a clarifier, and when it is added in a smallamount, it keeps the inclusion of impurities such as Fe, etc., fromdecreasing the light transmittance. Due to its strong oxidizingactivity, however, it promotes to deteriorate the molding surface of apress mold when press-molding is carried out. Further, when Sb₂O₃ isadded, the glass tends to be increasingly colored. The amount of Sb₂O₃to be added on the basis of a glass composition excluding Sb₂O₃ ispreferably 0 to 1%, more preferably 0 to 0.5%, still more preferably 0to 0.1%. Adding no Sb₂O₃, that is, being an Sb-free glass isparticularly preferred.

SnO₂ can be added as a clarifier. However, when it is added in an amountof over 1% on the basis of a glass composition excluding SnO₂, the glassis colored, and when the re-molding of the glass by heating andsoftening it, such as press-molding, is carried out, Sn constitutes astarting point for crystal germ, and a tendency to devitrification takesplace. The amount of SnO₂ to be added on the basis of a compositionexcluding SnO₂ is preferably 0 to 1%, more preferably 0 to 0.5%, andadding no SnO₂ is particularly preferred.

The optical glass of this invention has realized the optical propertiesof a high-refractivity low-dispersion while the glass stability ismaintained, and it obviates the incorporation of components such as Luand Hf. Since Lu and Hf are expensive components, the content of each ofLu₂O₃ and HfO₂ is preferably limited to 0 to 1%, more preferably, to 0to 0.5%. Incorporating no Lu₂O₃ and incorporating no HfO₂ areparticularly preferred, respectively.

Environmental impacts considered, further, it is preferred to introducenone of As, Pb, U, Th, Te and Cd.

For taking advantage of excellent light transmittance, it is preferredto introduce none of substances that are coloring factors such as Cu,Cr, V, Fe, Ni, Co, etc.

(Properties of Optical Glass)

The optical glass of this invention has a refractive index nd of 1.89 to2.0. When lenses are produced from the above optical glass, a glasshaving a higher refractive index ensures that the curve of a lenssurface can be moderated (the absolute value of a curvature radius isincreased) if the lens has a constant focal length, and there can beproduced an effect that the making of lenses is easier or that thecorrection of aberration is easier. Further, when an image-sensingoptical system or a projection optical system is constituted from acombination of a plurality of lenses, the optical system can bedownsized.

In the optical systems such as an image-sensing optical system and aprojection optical system, when an optical path is bent by the use of aprism for reducing an optical path length, a higher refractive index ofa glass constituting the prism is effective for reducing the opticalpath length. In the image-sensing optical system, the angle of view canbe increased. For the above reasons, the lower limit of the refractiveindex nd is determined as follows. On the other hand, when therefractive index is increased to excess, the glass stability decreases,and it tends to be difficult to produce the glass, so that the upperlimit of the refractive index nd is determined as follows. The lowerlimit of the refractive index nd is preferably 1.892, more preferably1.894, still more preferably 1.895, yet more preferably 1.90. The upperlimit thereof is preferably 1.98, more preferably 1.95, still morepreferably 1.94, yet more preferably 1.93.

The optical glass of this invention has an Abbe's number νd of 32 to 38.When a lens formed of the optical glass of this invention and a lensformed of a high-refractivity high-dispersion glass are combined, therecan be obtained a compact optical system for correcting chromaticaberration. In such an optical system for correction chromaticaberration, a larger difference between the Abbe's number of the opticalglass of this invention and the Abbe's number of the high-refractivityhigh-dispersion glass is advantageous for realizing excellent chromaticaberration correction. For this reason, the lower limit of the Abbe'snumber νd is adjusted to the above value. When it is sought to impartthe property of low dispersion excessively, the glass stability and themoldability of a molten glass decrease, and it is difficult to produce aglass. Therefore, the upper limit of the Abbe's number νd is adjusted tothe above value. The lower limit of the Abbe's number is preferably32.5, more preferably 33.0, still more preferably 33.5, yet morepreferably 34.0, further more preferably 34.5. The upper limit of theAbbe's number νd is preferably 37.9, more preferably 37.8, still morepreferably 37.7.

The refractive index of a glass having a smaller Abbe's number νd, i.e.,a glass having a higher dispersion can be more easily increased whilemaintaining the stability and the viscosity during the molding of amolten glass. However, even if the properties of higher-refractivitylower-dispersion within the above optical properties are imparted, theglass stability and moldability of a molten glass can be maintained, sothat there can be realized and optical glass that is in particularuseful in optical design. From this viewpoint, an optical glass havingoptical properties that satisfy the following expression (1) ispreferred, an optical glass having optical properties that satisfy thefollowing expression (2) is more preferred, an optical glass havingoptical properties that satisfy the following expression (3) is stillmore preferred, an optical glass having optical properties that satisfythe following expression (4) is yet more preferred, an optical glasshaving optical properties that satisfy the following expression (5) isfurther more preferred, and an optical glass having optical propertiesthat satisfy the following expression (6) is still further morepreferred.

nd≧2.54−0.02×νd  (1)

nd≧2.55−0.02×νd  (2)

nd≧2.56−0.02×νd  (3)

nd≧2.57−0.02×νd  (4)

nd≧2.58−0.02×νd  (5)

nd≧2.59−0.02×νd  (6)

When the ranges defined by the expressions (1) to (6) and the preferredlower limit of refractive index nd are combined, in the range of thisinvention, a range defined by

nd≧2.54−0.02×νd (in which νd>32.5), and

nd≧1.89 (in which νd≦32.5)

is preferred, a range defined by

nd≧22.55−0.02×νd (in which νd>33.0), and

nd≧1.89 (in which νd≦33.0)

is more preferred, a range defined by

nd≧22.56−0.02×νd (in which νd>33.5), and

nd≧1.89 (in which νd≦33.5)

is still more preferred, a range defined by

nd22.57−0.02×νd (in which νd>34.0), and

nd≧1.89 (in which νd≦34.0)

is yet more preferred, a range defined by

nd≧22.58−0.02×νd (in which νd>34.5), and

nd≧1.89 (in which νd≦34.5)

is further more preferred, and a range defined by

nd≧22.59−0.02×νd (in which νd>35.0), and

nd≧1.89 (in which νd≦35.0)

is still further more preferred.

The above embodiment is a range in which a refractive index of 1.89 ormore and the expressions (1) to (6) are established. The other fourranges, i.e., a range in which a refractive index of 1.892 or more andthe expressions (1) to (6) are established, a range in which arefractive index of 1.894 or more and the expressions (1) to (6) areestablished, a range in which a refractive index of 1.895 or more andthe expressions (1) to (6) are established, and a range in which arefractive index of 1.90 or more and the expressions (1) to (6) areestablished can be similarly defined.

On the other hand, for realizing far more excellent glass stability, anoptical glass having optical properties that satisfy the followingexpression (7) is preferred, an optical glass having optical propertiesthat satisfy the following expression (8) is more preferred, and anoptical glass having optical properties that satisfy the followingexpression (9) is still more preferred.

nd≦2.69−0.02×νd  (7)

nd≦2.68−0.02×νd  (8)

nd≦2.67−0.02×νd  (9)

When the ranges defined by the expressions (7) to (9) and the preferredupper limit of refractive index nd are combined, in the range of thisinvention, a range defined by

nd≦2.69−0.02×νd (in which νd>34.5), and

nd≦2.0 (in which νd≦34.5)

is preferred, a range defined by

nd≦2.68−0.02×νd (in which νd>34.0), and

nd≦2.0 (in which νd≦34.0)

is more preferred, and a range defined by

nd≦2.67−0.02×νd (in which νd>33.5), and

nd≦2.0 (in which νd≦33.5)

is still more preferred.

The above embodiment is a range in which a refractive index nd of 2.0 orless and the expressions (7) to (9) are established. The other fourranges, i.e., a range in which a refractive index of 1.98 or less andthe expressions (7) to (9) are established, a range in which arefractive index of 1.95 or less and the expressions (7) to (9) areestablished, a range in which a refractive index of 1.94 or less and theexpressions (7) to (9) are established and a range in which a refractiveindex of 1.93 or less and the expressions (7) to (9) are established canbe also similarly defined.

(Coloring of Glass)

The coloring degree λ70 of the optical glass of this invention is 430 nmor less. The coloring degree λ70 corresponds to a wavelength at which a10±0.1 mm thick glass having optically polished two opposite surfaces inparallel with each other exhibits a transmittance of 70% when measuredfor a spectral transmittance in the wavelength region of 280 nm to 700nm. The above spectral transmittance or the above transmittance is aquantity represented by I_(out)/I_(in) when light having an intensity ofI_(in) is caused to perpendicularly enter one of the above surfaces ofthe glass and light having an intensity of I_(out) comes out of theother surface after the glass transmits the light, and it is atransmittance including a surface reflection loss on the above surfaceof the glass.

The surface reflection loss increases with an increase in the refractiveindex of a glass. Therefore, a high-refractivity glass having a smallλ70 means that the coloring of the glass itself is remarkably reduced.When λ70 is adjusted to 430 nm or less, there can be provided an opticalelement for constituting an image-sensing optical system or projectionoptical system having an excellent color balance. In the image-sensingoptical system or projection optical system, a plurality of lenses areused for correcting various aberrations. There is therefore a problemthat when lenses formed of colored glasses are used, the transmittedlight quantity of the entire optical system is decreased. In particular,an interchangeable lens of a single-lens reflex camera has a largeaperture, so that the lens thickness is large, and when a colored lensis used, the transmitted light quantity is greatly decreased. Whenlenses are produced from the optical glass of this invention, asufficient transmitted light quantity can be secured even in one singlelens or the entire optical system, since the coloring thereof isremarkably reduced while it is a high-refractivity low-dispersion glass.Further, owning to a combination of its coloring that is reduced and thehigh-refractivity low-dispersion properties that it has, theimage-sensing optical system and projection optical system can bedownsized. For these reasons, the optical glass of this invention issuitable as an optical element material for constituting theimage-sensing optical system and projection optical system, and it issuitable in particular as an optical element material for constitutingan interchangeable lens of a single-lens reflex camera.

For coping with the above demands, an optical glass having λ70 in theabove range is required. In the optical glass of this invention,further, the coloring degree is preferably in a range in which λ70 is425 nm or less, more preferably in a range in which λ70 is 420 nm orless, still more preferably in a range in which λ70 is 415 nm or less,yet more preferably in a range in which λ70 is 410 nm or less, furthermore preferably in a range in which λ70 is 405 nm or less. The lowerlimit of λ70 is naturally restricted depending upon properties of theglass such as a refractive index and the composition of the glass.

In addition to the coloring degrees other than λ70, λ80 and λ5 may beemployed. λ80 is a wavelength at which a transmittance of 80 isexhibited, and λ5 is a wavelength at which a transmittance of 5% isexhibited.

(Viscosity of Glass at Liquidus Temperature)

In a high-refractivity glass, in particular a high-refractivitylow-dispersion glass, the temperature to be employed when a molten glassis caused to flow out and molded is generally increased for preventingits devitrification during molding of the molten glass. Therefore, themolten glass that is caused to flow out and molded has a very lowviscosity, and it is difficult to produce a high-quality glass highlyproductively.

When the temperature employed when a glass is caused to flow out ishigh, a specific easy-volatile glass component volatilizes from theglass surface having a high temperature, and the glass surface isaltered. As a result, an optically non-uniform portion called striae isformed in the glass surface. Further, when the viscosity that a glasshas when it is caused to flow out and molded is low, a surface of theglass that is caused to flow out is taken into an inside to cause striaewithin the glass. Further, when the temperature that the glass has whenit is caused to flow out is high, a mold in contact with the glasshaving a high temperature is likely to be thermally deteriorated andworn out.

When the viscosity of a high-refractivity low-dispersion glass at aliquidus temperature can be secured, the moldability of a molten glasscan be improved, and a high-quality glass can be supplied highlyproductively. Further, the inhibition of the liquidus temperature fromincreasing works advantageously to improve the productivity of ahigh-quality glass.

For these reasons, the optical glass of this invention is preferably anoptical glass having a viscosity, measured at its liquidus temperature,of 1 dPa·s or more. When the above viscosity property is imparted, themoldability of a molten glass of the high-refractivity low-dispersionglass can be remarkably improved. For more improving the abovemoldability, preferably, the viscosity at a liquidus temperature isadjusted to 1.2 dPa·s or more, more preferably, it is adjusted to 1.4dPa·s or more, still more preferably, it is adjusted to 1.6 dPa·s, yetmore preferably, it is adjusted to 2.0 dPa·s or more, further morepreferably, it is adjusted to 2.5 dPa·s or more. The upper limit of theviscosity at a liquidus temperature is naturally restricted dependingupon the component ranges of the above glass composition, while 30 dPa·sor less can be considered as a target.

From the above viewpoint, preferably, the liquidus temperature of theoptical glass of this invention is adjusted to 1,300° C. or lower, morepreferably it is adjusted to 1,280° C. or lower, still more preferablyit is adjusted to 1,250° C. The lower limit of the liquidus temperatureis naturally restricted depending upon the glass composition, while1,000° C. or higher can be considered as a target.

(Glass Transition Temperature)

In the optical glass of this invention, a plurality of components forimparting a high refractive index are introduced in such a way that theyare well-balanced, and it is ensured that the content of no specificcomponent for imparting a high refractive index is dominantly large.Since ZnO is introduced as an essential component, further, the glasstransition temperature of the optical glass can be kept low for ahigh-refractivity low-dispersion glass.

In the optical glass of this invention, the glass transition temperatureis preferably in the range of 710° C. or lower, more preferably 700° C.or lower, still more preferably 695° C. or lower. When the glasstransition temperature is kept low, the annealing temperature of theglass can be inhibited from increasing, and the thermal deteriorationand wearing of an annealing apparatus can be suppressed. Further, theheating temperature during the press-molding of the glass by re-heatingand softening can be kept low, and the thermal deterioration and wearingof a press-molding apparatus such as a press mold can be suppressed.Stainless steel is often used in an annealing furnace, a device fortransferring a glass in the annealing furnace and a press-moldingapparatus. Stainless steel has a deformation temperature around 700° C.,and when the glass transition temperature is controlled so that it is inthe above range, in particular 700° C. or lower, preferably 695° C. orlower, the deformation of stainless steel in the above steps can beprevented.

The lower limit of the glass transition temperature is naturallyrestricted depending upon the glass composition, while 650° C. or highercan be considered as a target.

(Devitrification Resistance During Re-Heating)

The optical glass of this invention is excellent in devitrificationresistance during the molding of the glass by re-heating. In a preferredembodiment of the optical glass of this invention, no precipitation of acrystal inside a glass is observed after a glass sample is held at 600to 800° C. for 10 minutes (primary treatment), thentemperature-increased to 820° C. to 900° C. and held at this temperaturefor 10 minutes (secondary treatment). FIG. 1 shows a relationshipbetween the temperatures of the primary treatment and secondarytreatment (re-heating) and the number density of crystals precipitatedinside a glass with regard to a glass obtained in Example 1. It is seenfrom FIG. 1 that since the number density of crystals during re-heatingis very low, the optical glass of this invention is excellent indevitrification resistance. When the above test is carried out, a glasssample obtained by cutting and polishing is preferred as such, and forexample, a glass sample having a size of 15×15×15 mm can be used. Thepresence or absence of crystal precipitation can be carried out byenlarging and observing an inside of a glass with an optical microscopeof 100 magnifications.

Further, when a glass sample (sample weight=6.05 g) obtained by cuttingand barrel-polishing was re-heated and press-molded, for example,according to a heating schedule shown in FIG. 2, no precipitation of acrystal was observed within the press-molded glass.

Since the optical glass of this invention so excellent indevitrification resistance, it is suitable as a material for apress-molding glass material from which a high-quality press-moldedproduct can be obtained.

(Process for Producing Optical Glass)

The process for producing the optical glass of this invention will beexplained below. For example, a non-vitrified raw material obtained byweighing and mixing compound raw materials in the form of a powder,i.e., oxides, carbonates, nitrates, sulfates, hydroxides, etc., inaccordance with an intended glass composition, or a vitrified rawmaterial obtained by weighing and mixing cullet raw materials obtainedby roughly melting the compound raw materials in accordance with anintended glass composition is supplied into a melting vessel made of aplatinum alloy, then heated and melted. The above raw material iscompletely melted to obtain a molten glass (glass melt), and then themolten glass is temperature-increased to clarify it. The clarified glassis stirred and homogenized with a stirrer, continuously supplied into aglass flow-out pipe, caused to flow out and rapidly cooled to solidnessto obtain a glass molded product.

The thus-obtained glass molded product is annealed to reduce or remove astrain in the molded product, and its refractive index is finelyadjusted as required, to obtain a material for an optical element or amaterial for a press-molding glass material.

The press-molding glass gob of this invention will be explained below.

[Press-Molding Glass Gob]

The press-molding glass gob of this invention is characteristicallyformed of the above optical glass of this invention. The form of the gobis so determined depending upon the form of a press-molded product thatthe gob can be easily press-molded. The mass of the gob is alsodetermined depending upon a press-molded product. In this invention, theglass excellent in stability is used, so that the glass does not easilydevitrify even when it is re-heated and softened, and high-qualitymolded products can be stably produced.

Production embodiments of a press-molding glass gob are as follows.

In a first production embodiment, a molten glass flowing out of a flowpipe is continuously cast into a mold arranged horizontally below theflow pipe, and is molded in a plate form having a constant thickness.The molded glass is continuously withdrawn in the horizontal directionthrough an opening portion provided on a side of the mold. The glassmolded material in the form of a plate is withdrawn with a beltconveyor. The glass molded material is withdrawn so as to ensure that ithas a constant thickness by setting the withdrawing speed of the beltconveyor at a constant speed, whereby the glass molded material having apredetermined thickness and a predetermined width can be obtained. Theglass molded material is carried into an annealing furnace with a beltconveyor to be gradually cooled. The gradually cooled glass moldedmaterial is cut or split in the thickness direction, and polished orbarrel-polished to obtain press-molding glass gobs.

In a second production embodiment, a molten glass is cast into acylindrical mold in place of the above mold and molded into a glassmolded material having the form of a column. The glass molded materialobtained by molding in the mold is withdrawn vertically downward at aconstant rate from an opening portion in the bottom of the mold. Thewithdrawing can be carried out at such a speed that the level of amolten glass is constant. After the glass molded material is graduallycooled, it is cut or split and polished or barrel-polished to obtainpress-molding glass gobs.

In a third production embodiment, a molding apparatus having a pluralityof molds arranged on the circumference of a circular turn table at equalintervals is placed below a flow pipe, the turn table is index-turned, amolten glass is supplied to a mold in one stop position that isdetermined to be a molten glass supply position (“cast position”hereinafter), the supplied molten glass is molded into a glass moldedmaterial, and then the glass molded material is taken out in apredetermined mold stop position (take-out position) different from thecast position. It can be determined by taking account of the turningspeed of the turn table, the cooling velocity of the glass, etc., whichstop position should be the take-out position. The molten glass can besupplied to the mold in the cast position by a method in which a moltenglass is dropped from the glass flow outlet of the flow pipe and a glassdrop is received with the above mold, a method in which the mold at astop in the cast position is caused to come near to the glass flowoutlet to support the lower end of a molten glass flow, a narrow portionis formed in the middle of the glass flow, the mold is rapidly movedvertically downward timely as predetermined to separate a molten glasslower than the narrow portion, and the molten glass is received on themold, a method in which a molten glass flow that is flowing out is cutwith a cutting blade and the separated molten glass mass is receivedwith the mold at a stop in the cast position, etc.

A known method can be used for molding on the mold. Above all, when theglass is molded while it is floated by applying a gas pressure upwardlyto the glass mass with a gas ejected upwardly from the mold, there canbe prevented the formation of creases on a glass molded material and thecracking of the glass molded material caused by a contact with the mold.

The form of the glass molded material can be a spherical form, aspheroidal form, a form having one axis of rotational symmetry andhaving two surfaces that face the axis direction of the axis of therotational symmetry and that have a convex form outwardly each, etc.,depending upon selection of a mold form or a method of ejecting theabove gas. These forms are suitable for a glass gob to be used forproducing an optical element such as a lens or an optical element blankby press-molding. The thus-obtained glass molded material can be used asa press-molding glass gob directly or after it is surface-polished orbarrel-polished.

[Optical Element]

The optical element of this invention will be explained below.

The optical element of this invention is characteristically formed ofthe above optical glass of this invention. The optical glass of thisinvention has high-refractivity low-dispersion properties and hasreduced or no contents of expensive components such as Ta₂O₅, GeO₂,etc., so that optical elements having an optically high value such asvarious lenses, prisms, etc., can be provided at a low cost.

Examples of the lens include various lenses such as a concave meniscuslens, a convex meniscus lens, a biconvex lens, a biconcave lens, aplano-convex lens, a plano-concave lens, etc., which have spherical oraspherical lens surfaces.

These lenses can correct chromatic aberration when combined with a lensformed of a high-refractivity high-dispersion glass, and they aresuitable as lenses for correcting chromatic aberration. Further, theyare lenses effective for downsizing an optical system.

Further, the optical element of this invention is formed of the opticalglass having a coloring degree λ70 of 430 nm or less, so that it issuitable as an optical element to be incorporated into an image-sensingoptical system that is required to have a high light transmittance, inparticular an interchangeable lens (e.g., an interchangeable lens of asingle-lens reflex camera) and a projection optical system.

Further, the prism has a high refractive index, and when it isincorporated into an image-sensing optical system, therefore, adownsized optical system having a wide angle of view can be realized bybending an optical path and directing it in the desired direction.

The optical-function surface of the optical element of this inventioncan be provided with a film that controls a light transmittance, such asan anti-reflection film, etc.

[Process for Producing Optical Element Blank]

The process for producing an optical element blank, provided by thisinvention, will be explained below.

The process for producing an optical element blank, provided by thisinvention, includes the following two embodiments.

(First Process for Producing an Optical Element Blank)

The first process for producing an optical element blank, provided bythis invention, is a process for producing an optical element blank tobe completed into an optical element by grinding and polishing, whichcomprises heating and softening the above press-molding glass gob ofthis invention and press-molding it.

According to this invention, there is used a gob formed of the aboveoptical glass of this invention that is excellent in devitrificationresistance when it is re-heated, so that an optical element blank can beproduced without devitrifying it. Since the glass having reducedcoloring is used, further, there can be produced a blank for obtainingan optical element that is sufficient in transmitted light quantity andexcellent in color balance.

The optical element blank refers to a glass molded material having aform that is obtained by adding a processing margin to be removed bygrinding and polishing to a form of an intended optical element and thatis similar to the form of the optical element.

When an optical element blank is produced, there is prepared a pressmold having molding surfaces that are the inverse of the above blank inform. The press mold is composed of mold parts including an upper moldmember, a lower mold member and optionally a sleeve member, and themolding surfaces of the upper and lower mold members are provided withthe above forms, or when the sleeve member is used, the molding surfaceof the sleeve member is provided with the above forms.

Then, a powder mold release agent such as boron nitride, or the like, isapplied to the surface of the press-molding glass gob, the press-moldingglass gob is introduced to the lower mold member preheated after it isheated and softened, and it is pressed with the lower mold member andthe opposing upper mold member to mold it into an optical element blank.

Then, the optical element blank is released and taken out of the pressmold, and it is annealing-treated. By the annealing-treatment, a strainwithin the glass is reduced, and optical properties such as a refractiveindex, etc., are brought into desired values.

Those which are known can be applied to the heating conditions andpress-molding conditions for the glass gob, materials to be used for thepress-mold, etc. The above steps can be carried out in atmosphere.

(Second Process for Producing an Optical Element)

The second process for producing an optical element blank, provided bythis invention, is a process for producing an optical element blank tobe completed into an optical element by grinding and polishing, whichcomprises melting glass raw materials, press-molding the resultantmolten glass and thereby producing an optical element blank formed ofthe above optical glass of this invention.

The press mold is composed of mold parts such as an upper mold member, alower mold member and optionally a sleeve member. The molding surfacesof the press mold are processed to ensure that they have forms that arethe inverse of the forms of the above optical element blank as describedabove.

A powder mold release agent such as boron nitride, or the like, isuniformly applied onto the molding surface of the lower mold member, amolten glass obtained by the above process for producing an opticalglass is caused to flow out onto the molding surface of the lower moldmember, and when the amount of the molten glass on the lower mold memberbecomes a desired amount, the molten glass flow is cut with a cuttingblade called shears. After a molten glass mass is so obtained on thelower mold member, the lower mold member with the molten glass mass onit is moved to a position where the upper mold member is on standbyabove, and the molten glass gob is pressed with the upper and lower moldmembers into an optical element blank.

Then, the optical element blank is released and taken out of the pressmold, and it was annealing-treated. By the annealing-treatment, a strainwithin the glass is reduced, and optical properties such as a refractiveindex, etc., are brought into desired values.

Those which are known can be applied to the heating conditions andpress-molding conditions for the glass gob, materials to be used for thepress-mold, etc. The above steps can be carried out in atmosphere. Inthe second process for producing an optical element blank, a blank canbe produced without devitrifying the glass. Further, there can beprovided a blank that gives an optical element that secures a sufficienttransmitted light quantity.

The process for producing an optical element, provided by thisinvention, will be explained below.

[Process for Producing Optical Element]

The process for producing an optical element, provided by thisinvention, can be largely classified into two embodiments.

A first embodiment of the process for producing an optical element (tobe referred to as “optical element production process I” hereinafter),provided by this invention, comprises producing an optical element blankaccording to the above process of this invention and grinding andpolishing the optical element blank. Known methods can be applied to thegrinding and polishing. The optical element production process I issuitable for producing a spherical lens, a prism, etc.

A second embodiment of the process for producing an optical element (tobe referred to as “optical element production process II” hereinafter),provided by this invention, is a process for producing an opticalelement, which comprises heating the above press-molding glass gob ofthis invention and precision press-molding the same. The precisionpress-molding can use a known press mold, and a known molding method canbe applied thereto. The optical element production process II issuitable for producing an aspherical lens, a microlens, a diffractiongrating, etc.

EXAMPLES

This invention will be explained with reference to Examples hereinafter,while this invention shall not be limited by these Examples.

Example 1

Glasses Nos. 1 to 22 having compositions shown in Tables 1 to 6 wereobtained as follows. Carbonate, nitrates, sulfates, hydroxides, oxides,boric acid, etc., were used as raw materials, powders of these rawmaterials were weighed and fully mixed to obtain a raw material mixture,the raw material mixture was placed in a crucible formed of platinum,heated at 1,200 to 1,400° C. for 1 to 3 hours to melt it, and a glassmelt was clarified and stirred to prepare a homogeneous molten glass.The molten glass was cast into a preheated mold and rapidly cooled, andthe glass was held at a temperature in the vicinity of its glasstransition temperature for 2 hours and gradually cooled. In this manner,optical glasses Nos. 1 to 11 were obtained. No precipitation of acrystal was recognized in any one of these glasses.

Properties of each glass were measured by the following methods. Tables1 to 6 show the results.

(1) Refractive index nd and Abbe's number νd

A cooled optical glass was measured at a temperature decrease rate of30° C. per hour.

(2) Glass transition temperature Tg

Measured with a thermomechanical analyzer under conditions of atemperature elevation rate of 4° C./minute.

(3) Liquidus temperature LT

A glass was placed in a furnace heated to a predetermined temperatureand held therein for 2 hours, followed by cooling, and an inside of theglass was observed through an optical microscope of 100 magnifications.A liquidus temperature was determined on the basis of whether or not ithad a crystal.

(4) Viscosity at liquidus temperature

A viscosity was measured according to Viscosity JIS Standard Z8803 by aviscosity measurement method using a coaxial double cylinder rotationalviscometer.

(5) Specific gravity

Measured by an Archimedean method.

(6) λ70, λ80 and λ5

A 10±0.1 mm thick glass sample having two optically polished surfacesopposite to each other was measured for a spectral transmittance, andeach was calculated on the basis of the results.

(7) Partial dispersion ratio P_(g,F),

Refractive indices nF, n_(c) and ng were measured, and it was calculatedon the basis of the results.

TABLE 1 No. 1 2 3 4 Composition SiO₂ 8.11 8.03 7.54 7.53 [mass %] B₂O₃11.02 10.55 11.47 11.64 La₂O₃ 43.95 43.53 44.32 43.42 Gd₂O₃ 10.34 10.7110.43 11.37 Y₂O₃ 2.34 3.48 2.36 2.36 Yb₂O₃ 0.00 0.00 0.00 0.00 ZnO 5.495.44 5.54 4.68 TiO₂ 6.22 6.16 6.27 6.26 Nb₂O₅ 6.28 6.22 6.33 7.01 ZrO₂5.05 4.69 5.74 5.73 WO₃ 1.20 1.19 0.00 0.00 Li₂O 0.00 0.00 0.00 0.00Na₂O 0.00 0.00 0.00 0.00 K₂O 0.00 0.00 0.00 0.00 MgO 0.00 0.00 0.00 0.00CaO 0.00 0.00 0.00 0.00 SrO 0.00 0.00 0.00 0.00 BaO 0.00 0.00 0.00 0.00Ta₂O₅ 0.00 0.00 0.00 0.00 GeO₂ 0.00 0.00 0.00 0.00 Bi₂O₃ 0.00 0.00 0.000.00 Al₂O₃ 0.00 0.00 0.00 0.00 Total 100.00 100.00 100.00 100.00 Sb₂O₃based on composition 0.10 0.10 0.10 0.10 excluding Sb₂O₃ SiO₂ + B₂O₃19.13 18.58 19.01 19.17 SiO₂/B₂O₃ 0.74 0.76 0.66 0.65 La₂O₃ + Gd₂O₃ +Y₂O₃ 56.63 57.72 57.11 57.15 (Gd₂O₃ + Y₂O₃)/(La₂O₃ + 0.22 0.25 0.22 0.24Gd₂O₃ + Y₂O₃) TiO₂ + Nb₂O₅ 12.50 12.38 12.60 13.27 Li₂O + Na₂O + K₂O0.00 0.00 0.00 0.00 MgO + CaO + SrO + BaO 0.00 0.00 0.00 0.00Gd₂O₃/(Gd₂O₃ + Y₂O₃) 0.82 0.75 0.82 0.83 Properties nd 1.90757 1.91071.90928 1.91036 vd 34.96 35.12 35.3 35.03 P_(g,F) 0.5832 0.58619 0.585790.58369 λ80 [nm] 497 490 500 494 λ70 [nm] 426 422 423 422 λ5 [nm] 360359 358 359 Glass transition temperature [° C.] 683 688 683 686 Liquidustemperature [° C.] 1200 1220 1190 1190 Viscosity at liquidus — — 3.083.12 temperature [dPa · s] Specific gravity 4.99 5.04 4.99 4.98

TABLE 2 No. 5 6 7 8 Composition SiO₂ 7.52 6.93 6.31 6.92 [mass %] B₂O₃11.49 12.03 12.44 12.03 La₂O₃ 43.34 43.52 43.65 43.49 Gd₂O₃ 11.35 11.4011.43 11.39 Y₂O₃ 2.36 2.37 2.37 2.60 Yb₂O₃ 0.00 0.00 0.00 0.00 ZnO 5.094.69 4.70 4.69 TiO₂ 6.13 6.28 6.29 6.11 Nb₂O₅ 7.00 7.03 7.05 7.03 ZrO₂5.72 5.75 5.76 5.74 WO₃ 0.00 0.00 0.00 0.00 Li₂O 0.00 0.00 0.00 0.00Na₂O 0.00 0.00 0.00 0.00 K₂O 0.00 0.00 0.00 0.00 MgO 0.00 0.00 0.00 0.00CaO 0.00 0.00 0.00 0.00 SrO 0.00 0.00 0.00 0.00 BaO 0.00 0.00 0.00 0.00Ta₂O₅ 0.00 0.00 0.00 0.00 GeO₂ 0.00 0.00 0.00 0.00 Bi₂O₃ 0.00 0.00 0.000.00 Al₂O₃ 0.00 0.00 0.00 0.00 Total 100.00 100.00 100.00 100.00 Sb₂O₃based on composition 0.10 0.10 0.10 0.10 excluding Sb₂O₃ SiO₂ + B₂O₃19.01 18.96 18.75 18.95 SiO₂/B₂O₃ 0.65 0.58 0.51 0.58 La₂O₃ + Gd₂O₃ +Y₂O₃ 57.05 57.29 57.45 57.48 (Gd₂O₃ + Y₂O₃)/(La₂O₃ + 0.24 0.24 0.24 0.24Gd₂O₃ + Y₂O₃) TiO₂ + Nb₂O₅ 13.13 13.31 13.34 13.14 Li₂O + Na₂O + K₂O0.00 0.00 0.00 0.00 MgO + CaO + SrO + BaO 0.00 0.00 0.00 0.00Gd₂O₃/(Gd₂O₃ + Y₂O₃) 0.83 0.83 0.83 0.81 Properties nd 1.90994 1.912311.91389 1.91107 vd 35.12 34.97 34.89 35.07 P_(g,F) 0.5851 0.582980.58228 0.58045 λ80 [nm] 495 492 494 498 λ70 [nm] 422 422 423 423 λ5[nm] 358 359 359 359 Glass transition temperature [° C.] 685 686 681 685Liquidus temperature [° C.] 1190 1175 1180 1175 Viscosity at liquidus —3.2 — 3.31 temperature [dPa · s] Specific gravity 4.98 5.00 5.01 5.00

TABLE 3 No. 9 10 11 12 Composition SiO₂ 6.92 6.04 6.01 6.63 [mass %]B₂O₃ 12.03 12.70 12.64 11.53 La₂O₃ 43.49 43.08 42.86 40.06 Gd₂O₃ 11.3911.51 11.45 10.92 Y₂O₃ 2.60 2.39 2.38 2.49 Yb₂O₃ 0.00 0.00 0.00 0.00 ZnO4.69 4.74 4.71 6.13 TiO₂ 6.11 6.34 6.31 4.25 Nb₂O₅ 7.03 7.10 7.06 1.40ZrO₂ 5.74 5.80 5.77 5.50 WO₃ 0.00 0.00 0.00 0.00 Li₂O 0.00 0.00 0.000.00 Na₂O 0.00 0.00 0.00 0.00 K₂O 0.00 0.00 0.00 0.00 MgO 0.00 0.00 0.000.00 CaO 0.00 0.30 0.00 0.00 SrO 0.00 0.00 0.00 0.00 BaO 0.00 0.00 0.810.00 Ta₂O₅ 0.00 0.00 0.00 11.09 GeO₂ 0.00 0.00 0.00 0.00 Bi₂O₃ 0.00 0.000.00 0.00 Al₂O₃ 0.00 0.00 0.00 0.00 Total 100.00 100.00 100.00 100.00Sb₂O₃ based on composition 0.00 0.00 0.00 0.00 excluding Sb₂O₃ SiO₂ +B₂O₃ 18.95 18.74 18.65 18.16 SiO₂/B₂O₃ 0.58 0.48 0.48 0.58 La₂O₃ +Gd₂O₃ + Y₂O₃ 57.48 56.98 56.69 53.47 (Gd₂O₃ + Y₂O₃)/(La₂O₃ + 0.24 0.240.24 0.25 Gd₂O₃ + Y₂O₃) TiO₂ + Nb₂O₅ 13.14 13.44 13.37 5.65 Li₂O +Na₂O + K₂O 0.00 0.00 0.00 0.00 MgO + CaO + SrO + BaO 0.00 0.30 0.81 0.00Gd₂O₃/(Gd₂O₃ + Y₂O₃) 0.81 0.83 0.83 0.81 Properties nd 1.91107 1.912711.9123 1.8964 vd 35.07 35.05 34.99 37.32 P_(g,F) 0.58045 0.58833 0.585730.57993 λ80 [nm] 500 485 485 469 λ70 [nm] 405 405 404 395 λ5 [nm] 351351 351 346 Glass transition temperature [° C.] 685 — — — Liquidustemperature [° C.] 1175 — — 1200 Viscosity at liquidus 3.31 — — —temperature [dPa · s] Specific gravity 5.00 4.99 5.00 5.24

TABLE 4 No. 13 14 15 16 Composition SiO₂ 6.64 6.58 6.68 6.92 [mass %]B₂O₃ 11.54 11.45 11.61 11.63 La₂O₃ 41.72 43.02 43.60 43.79 Gd₂O₃ 10.9210.83 10.99 11.49 Y₂O₃ 2.49 2.47 2.51 2.60 Yb₂O₃ 0.00 0.00 0.00 0.00 ZnO5.31 4.46 5.34 4.69 TiO₂ 4.25 4.22 4.28 6.11 Nb₂O₅ 2.74 2.71 2.75 7.03ZrO₂ 5.51 5.46 5.54 5.74 WO₃ 0.00 0.00 0.00 0.00 Li₂O 0.00 0.00 0.000.00 Na₂O 0.00 0.00 0.00 0.00 K₂O 0.00 0.00 0.00 0.00 MgO 0.00 0.00 0.000.00 CaO 0.00 0.00 0.00 0.00 SrO 0.00 0.00 0.00 0.00 BaO 0.00 0.00 0.000.00 Ta₂O₅ 8.88 8.80 6.70 0.00 GeO₂ 0.00 0.00 0.00 0.00 Bi₂O₃ 0.00 0.000.00 0.00 Al₂O₃ 0.00 0.00 0.00 0.00 Total 100.00 100.00 100.00 100.00Sb₂O₃ based on composition 0.00 0.00 0.00 0.00 excluding Sb₂O₃ SiO₂ +B₂O₃ 18.18 18.03 18.29 18.55 SiO₂/B₂O₃ 0.58 0.57 0.58 0.60 La₂O₃ +Gd₂O₃ + Y₂O₃ 55.13 56.32 57.10 57.88 (Gd₂O₃ + Y₂O₃)/(La₂O₃ + 0.24 0.240.24 0.24 Gd₂O₃ + Y₂O₃) TiO₂ + Nb₂O₅ 6.99 6.93 7.03 13.14 Li₂O + Na₂O +K₂O 0.00 0.00 0.00 0.00 MgO + CaO + SrO + BaO 0.00 0.00 0.00 0.00Gd₂O₃/(Gd₂O₃ + Y₂O₃) 0.81 0.81 0.81 0.82 Properties nd 1.8997 1.901491.89766 1.91458 vd 37.04 37.1 37.4 34.87 P_(g,F) 0.5776 0.57654 0.577080.58063 λ80 [nm] 472 477 494 491 λ70 [nm] 397 397 398 409 λ5 [nm] 347346 346 352 Glass transition temperature [° C.] 685 691 684 685 Liquidustemperature [° C.] 1190 1190 1200 1185 Viscosity at liquidus — — — —temperature [dPa · s] Specific gravity 5.21 5.23 5.19 5.02

TABLE 5 No. 17 18 19 20 Composition SiO₂ 6.92 6.92 6.92 6.92 [mass %]B₂O₃ 11.83 11.53 12.83 12.43 La₂O₃ 43.69 43.99 42.69 43.20 Gd₂O₃ 11.3911.39 11.39 11.28 Y₂O₃ 2.60 2.60 2.60 2.60 Yb₂O₃ 0.00 0.00 0.00 0.00 ZnO4.69 4.69 4.69 4.69 TiO₂ 6.11 6.11 6.11 6.11 Nb₂O₅ 7.03 7.03 7.03 7.03ZrO₂ 5.74 5.74 5.74 5.74 WO₃ 0.00 0.00 0.00 0.00 Li₂O 0.00 0.00 0.000.00 Na₂O 0.00 0.00 0.00 0.00 K₂O 0.00 0.00 0.00 0.00 MgO 0.00 0.00 0.000.00 CaO 0.00 0.00 0.00 0.00 SrO 0.00 0.00 0.00 0.00 BaO 0.00 0.00 0.000.00 Ta₂O₅ 0.00 0.00 0.00 0.00 GeO₂ 0.00 0.00 0.00 0.00 Bi₂O₃ 0.00 0.000.00 0.00 Al₂O₃ 0.00 0.00 0.00 0.00 Total 100.00 100.00 100.00 100.00Sb₂O₃ based on composition 0.00 0.00 0.00 0.00 excluding Sb₂O₃ SiO₂ +B₂O₃ 18.75 18.45 19.75 19.35 SiO₂/B₂O₃ 0.58 0.60 0.54 0.56 La₂O₃ +Gd₂O₃ + Y₂O₃ 57.68 57.98 56.68 57.08 (Gd₂O₃ + Y₂O₃)/(La₂O₃ + 0.24 0.240.24 0.24 Gd₂O₃ + Y₂O₃) TiO₂ + Nb₂O₅ 13.14 13.14 13.14 13.14 Li₂O +Na₂O + K₂O 0.00 0.00 0.00 0.00 MgO + CaO + SrO + BaO 0.00 0.00 0.00 0.00Gd₂O₃/(Gd₂O₃ + Y₂O₃) 0.81 0.81 0.81 0.81 Properties nd 1.91261 1.914971.90443 1.90636 vd 35.01 34.92 35.26 35.23 P_(g,F) 0.58343 0.581680.58441 0.58259 λ80 [nm] 487 493 479 482 λ70 [nm] 407 408 405 405 λ5[nm] 351 351 352 352 Glass transition temperature [° C.] 683 684 686 687Liquidus temperature [° C.] 1175 1185 1175 1175 Viscosity at liquidus —— — — temperature [dPa · s] Specific gravity 5.01 5.03 4.94 4.96

TABLE 6 No. 21 22 Composition SiO₂ 6.96 6.98 [mass %] B₂O₃ 11.90 12.14La₂O₃ 43.36 42.99 Gd₂O₃ 11.46 11.49 Y₂O₃ 2.62 2.62 Yb₂O₃ 0.00 0.00 ZnO4.71 4.73 TiO₂ 6.15 6.16 Nb₂O₅ 7.07 7.10 ZrO₂ 5.77 5.79 WO₃ 0.00 0.00Li₂O 0.00 0.00 Na₂O 0.00 0.00 K₂O 0.00 0.00 MgO 0.00 0.00 CaO 0.00 0.00SrO 0.00 0.00 BaO 0.00 0.00 Ta₂O₅ 0.00 0.00 GeO₂ 0.00 0.00 Bi₂O₃ 0.000.00 Al₂O₃ 0.00 0.00 Total 100.00 100.00 Sb₂O₃ based on composition 0.000.00 excluding Sb₂O₃ SiO₂ + B₂O₃ 18.86 19.12 SiO₂/B₂O₃ 0.58 0.57 La₂O₃ +Gd₂O₃ + Y₂O₃ 57.44 57.10 (Gd₂O₃ + Y₂O₃)/(La₂O₃ + 0.25 0.25 Gd₂O₃ + Y₂O₃)TiO₂ + Nb₂O₅ 13.22 13.26 Li₂O + Na₂O + K₂O 0.00 0.00 MgO + CaO + SrO +BaO 0.00 0.00 Gd₂O₃/(Gd₂O₃ + Y₂O₃) 0.81 0.81 Properties nd 1.912361.91051 vd 35.01 35.06 P_(g,F) 0.58327 0.58253 λ80 [nm] 487 486 λ70 [nm]404 403 λ5 [nm] 352 352 Glass transition temperature 683 682 [° C.]Liquidus temperature [° C.] 1175 1175 Viscosity at liquidus — —temperature [dPa · s] Specific gravity 5.00 4.99

Example 2

Press-molding glass gobs formed of the optical glasses Nos. 1 to 22 ofExamples 1 were produced in the following manner.

Glass raw materials were formulated so as to give one the above glasses,the formulated materials were charged into a crucible formed ofplatinum, heated and melted, and the glass melt was clarified andstirred to give a molten glass. Then, the molten glass was caused toflow out from a flow pipe at a constant flow rate, cast into a moldarranged horizontally below the flow pipe and molded into a glass platehaving a constant thickness. The thus-formed glass plate wascontinuously withdrawn in the horizontal direction from an openingportion provided in a side of the mold, carried into an annealingfurnace by means of a belt conveyor and gradually cooled.

The gradually cooled glass plate was cut or split to prepare glasspieces, and these glass pieces were barrel-polished to obtainpress-molding glass gobs.

In addition, there may be employed a constitution in which a cylindricalmold is arranged below the flow pipe, the molten glass is cast into themold and molded into a columnar glass, the columnar glass is withdrawnvertically downward from the opening portion of bottom of the mold at aconstant rate, then gradually cooled and cut or split to prepare glasspieces, and these glass pieces are barrel-polished to obtainpress-molding glass gobs.

Example 3

A molten glass was caused to flow out of the flow pipe in the samemanner as in Example 2, the lower end of flowing molten glass wasreceived with a mold, the mold was rapidly moved downward to cut themolten glass flow by surface tension, and a desired amount of a moltenglass mass was obtained on the mold. A gas pressure was applied to theglass by ejecting a gas from the mold, and the glass was molded into aglass mass while it was floated. It was taken out of the mold andannealed. The glass mass was barrel-polished, and press-molding glassgobs were obtained in the above manner.

Example 4

A mold release agent that was a boron nitride powder was uniformlyapplied to the entire surface of each of the press-molding glass gobsobtained in Example 3, and these gobs were softened by heating accordingto a heating schedule shown in FIG. 2 and press-molded to obtain blanksof various lenses such as a concave meniscus lens, a convex meniscuslens, a biconvex lens, a biconcave lens, a plano-convex lens, aplano-concave lens, etc., and a prism.

Example 5

Molten glasses were prepared in the same manner as in Example 2, andeach molten glass was supplied on the molding surface of a lower moldmember to which a mold release agent that was a boron nitride powder hadbee applied. When the amount of each molten glass on the lower moldmember became a desired amount, the molten glass flow was cut with acutting blade.

Each molten glass mass obtained on the lower mold member in the abovemanner was pressed with an upper mold member and the lower mold memberto obtain blanks of various lenses such as a concave meniscus lens, aconvex meniscus lens, a biconvex lens, a biconcave lens, a plano-convexlens, a plano-concave lens, etc., and a prism.

Example 6

The blanks made in Examples 4 and 5 were annealed to ensure that a stainin each glass was reduced and that optical properties such as arefractive index were brought into desired values.

Then, the blanks were ground and polished to produce various lenses suchas a concave meniscus lens, a convex meniscus lens, a biconvex lens, abiconcave lens, a plano-convex lens, a plano-concave lens, etc., and aprism. The thus-obtained optical elements may be surface-coated with ananti-reflection film each.

Example 7

Glass plates and columnar glasses were prepared in the same manner as inExample 2, and the thus-obtained glass molded materials were annealed toensure that a stain in each material was reduced and that opticalproperties such as a refractive index were brought into desired values.

Then, these glass molded materials were cut, ground and polished toproduce blanks of various lenses such as a concave meniscus lens, aconvex meniscus lens, a biconvex lens, a biconcave lens, a plano-convexlens, a plano-concave lens, etc., and a prism. The thus-obtained opticalelements may be surface-coated with an anti-reflection film each.

Example 8

The glass gobs prepared in Example 2 were softened by heating andprecision press-molded with a press mold to obtain various asphericallenses such as a concave meniscus lens, a convex meniscus lens, abiconvex lens, a biconcave lens, etc. The thus-obtained lenses may besurface-coated with an anti-reflection film each.

INDUSTRIAL UTILITY

This invention is an optical glass that can be stably supplied andcoloring remarkably reduced and that has excellent glass stability andhigh-refractivity low-dispersion properties, and it is suitable forpress-molding glass gobs, optical element blanks and optical elements.

1-15. (canceled)
 16. An optical glass comprising, denoted by mass %, 5to 12% of SiO₂ 9 to 15% of B₂O₃, 32 to 55% of La₂O₃, 56.32 to 65% oftotal of La₂O₃, Gd₂O₃ and Y₂O₃ (comprising equal to or greater than 0.1%of Gd₂O₃), 1 to 8% of ZnO, 1 to 20% of total of TiO₂ and Nb₂O₅(comprising equal to or greater than 0.1% of each of TiO₂ and Nb₂O₅),0.5 to 15% of ZrO₂, 0 to 12% of Ta₂O₅, 0 to 5% of GeO₂, wherein the massratio of the content of SiO₂ to the content of B₂O₃, (SiO₂/B₂O₃), isfrom 0.3 to 1.0, and the mass ratio of the total content of Gd₂O₃ andY₂O₃ to the total content of La₂O₃, Gd₂O₃ and Y₂O₃,(Gd₂O₃+Y₂O₃)/(La₂O₃+Gd₂O₃+Y₂O₃), is from 0.05 to 0.6, the optical glasshaving a refractive index nd of 1.90 to 2.0 and an Abbe's number νd of32 to 38 and having a coloring degree λ70 of 430 nm or less.
 17. Theoptical glass according to claim 16, which comprises none of Li₂O, Na₂O,and K₂O.
 18. The optical glass according to claim 16, which comprises,denoted by mass %, 0.1 to 25% of Gd₂O₃.
 19. The optical glass accordingto 16, which comprises, denoted by mass %, 0.1 to 15% of TiO₂, 0.1 to15% of Nb₂O₅. 20 The optical glass according to claim 16, which has aTa₂O₅ content of 0 to 10 mass %.
 21. The optical glass according toclaim 16, which is a Ge-free glass.
 22. The optical glass according toclaim 16, wherein the mass ratio of the content of SiO₂ to the contentof B₂O₃, (SiO₂/B₂O₃), is from 0.3 to 0.9.
 23. The optical glassaccording to claim 16, wherein the mass ratio of the total content ofGd₂O₃ and Y₂O₃ to the total content of La₂O₃, Gd₂O₃ and Y₂O₃,(Gd₂O₃+Y₂O₃)/(La₂O₃+Gd₂O₃+Y₂O₃), is from 0.1 to 0.5.
 24. The opticalglass according to claim 16, wherein the mass ratio of the content ofGd₂O₃ to the total content of Gd₂O₃ and Y₂O₃, (Gd₂O₃)/(Gd₂O₃+Y₂O₃), isfrom 0.1 to
 1. 25. The optical glass according to claim 16, which has acoloring degree λ70 of 425 nm or less.
 26. The optical glass accordingto claim 16, which has a liquidus temperature of 1,300° C. or lower. 27.The optical glass according to claim 16, which has a glass transitiontemperature of 710° C. or lower.
 28. The optical glass according toclaim 16, which has a glass transition temperature of 650° C. or higher.29. The optical glass according to claim 16, which has a glasstransition temperature of 681° C. or higher.
 30. The optical glassaccording to claim 16, which has a specific gravity of 4.94 to 5.24. 31.A press-molding glass gob formed of the optical glass according to claim16.
 32. An optical element formed of the optical glass according toclaim
 16. 33. An optical element formed of the optical glass accordingto claim
 1. 34. A process for producing an optical element blank that iscompleted into an optical element by grinding and polishing, whichcomprises heating, softening, and press-molding the press-molding glassgob according to claim
 17. 35. A process for producing an opticalelement blank that is completed into an optical element by grinding andpolishing, which comprises melting glass raw materials, press-moldingthe resultant molten glass and producing the optical element blankformed of the optical glass according to claim
 1. 36. A process forproducing an optical element, which comprises producing an opticalelement blank by the process according to claim 19, and grinding andpolishing the optical element blank.
 37. A process for producing anoptical element, which comprises heating the press-molding glass gobaccording to claim 17 and precision press-molding the same.